CN112077430A - Method for diffusion welding and welded product - Google Patents
Method for diffusion welding and welded product Download PDFInfo
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- CN112077430A CN112077430A CN202010978544.0A CN202010978544A CN112077430A CN 112077430 A CN112077430 A CN 112077430A CN 202010978544 A CN202010978544 A CN 202010978544A CN 112077430 A CN112077430 A CN 112077430A
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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Abstract
The invention relates to the technical field of welding, in particular to a diffusion welding method and a welding finished product. The embodiment of the invention provides a diffusion welding method, which comprises the following steps: and performing diffusion welding on the IC10 single crystal and the nickel-based high-temperature alloy by using AlCoCrFeNi series high-entropy alloy as an intermediate layer. The diffusion welding can reduce the formation of carbide, improve the strength of the welded material, reduce the dilution of alloy solute in the near seam area of the base material and improve the performance of the near seam area.
Description
Technical Field
The invention relates to the technical field of welding, in particular to a diffusion welding method and a welding finished product.
Background
The direct solid-phase diffusion welding is a precise welding method which is used for realizing metallurgical bonding by mutually contacting the welding surfaces of materials to be welded at a certain temperature and under a certain pressure and further mutually diffusing and permeating atoms of a bonding layer for a certain time through microscopic plastic deformation. In the solid-phase diffusion welding process, the base metal is not melted, and the occurrence of joint cracks is avoided. With the development of the diffusion welding process, the diffusion welding with the added ultrathin middle layer is introduced, the existence of the middle layer can increase the concentration gradient of the parent metal/the middle layer, accelerate the diffusion of atoms in the parent metal to a welding line, quickly improve the alloying degree and improve the stability of the quality of a joint.
However, when the nickel-based superalloy is connected by solid-phase diffusion welding, the following main problems exist: when the direct solid-phase diffusion welding is carried out, carbides which influence the joint bonding strength are generated at the joint due to the existence of the C element; when pure metal is used as an intermediate layer for diffusion welding, the gamma' phase generated by the joint can limit the strength of the joint and a large amount of interdiffusion of high-concentration gradient elements can dilute alloy solute in a near-seam region of a base material, recrystallization of the base material can occur, and the performance of the near-seam region can be weakened; the joint generates a polycrystalline phase (e.g., γ' phase) having a lower strength than the base material.
In view of this, the invention is particularly proposed.
Disclosure of Invention
The invention aims to provide a diffusion welding method and a welding finished product. The diffusion welding can reduce the formation of carbide, improve the strength of the welded material, reduce the dilution of alloy solute in the near seam area of the base material and improve the performance of the near seam area.
The invention is realized by the following steps:
in a first aspect, an embodiment of the present invention provides a method of diffusion welding, including: and performing diffusion welding on the IC10 single crystal and the nickel-based high-temperature alloy by using AlCoCrFeNi series high-entropy alloy as an intermediate layer.
In an alternative embodiment, the composition of the AlCoCrFeNi-based high entropy alloy comprises the following components in atomic percent: 0.3 at% of Al, and the balance of Co, Cr, Fe and Ni, wherein the atomic ratio of Co, Cr, Fe and Ni is 1:1: 1.
In an alternative embodiment, the grain diameter of the AlCoCrFeNi-based high entropy alloy is 1-10 microns.
In an alternative embodiment, the preparation process of the AlCoCrFeNi-based high-entropy alloy comprises the following steps: mixing an aluminum source, a cobalt source, a chromium source, an iron source and a nickel source, smelting, and then carrying out heat treatment to form the AlCoCrFeNi high-entropy alloy.
In an alternative embodiment, the conditions for heat-treating the AlCoCrFeNi-based high entropy alloy include: the homogenization temperature is 1200 ℃, the homogenization time is 4 hours, the rolling is reduced by 60 percent, the temperature for heat preservation after rolling is 850 ℃, and the heat preservation time is 1 hour.
In an alternative embodiment, the IC10 single crystal comprises DD5 single crystal.
In an alternative embodiment, the nickel-base superalloy is an FGH98 powder alloy.
In an alternative embodiment, the conditions for diffusion welding are: the welding temperature is 900-.
In a second aspect, embodiments of the present invention provide a welded product, which is prepared by the method of diffusion welding according to any one of the foregoing embodiments.
The invention has the following beneficial effects: the embodiment of the invention uses AlCoCrFeNi series high-entropy alloy as the intermediate layer to perform diffusion welding on IC10 single crystal and nickel-based high-temperature alloy, and has the following advantages:
(1) the AlCoCrFeNi series high-entropy alloy can dissolve a small amount of C element in a solid manner without precipitating carbide, namely the AlCoCrFeNi series high-entropy alloy intermediate layer can inhibit the precipitation of carbide at an interface;
(2) AlCoCrFeNi series high-entropy alloy and gamma 'phase interface atoms are in a coherent relationship, so that the high-strength combination of the AlCoCrFeNi series high-entropy alloy intermediate layer and gamma' phase in IC10 single crystal and nickel-based high-temperature alloy is ensured;
(3) the AlCoCrFeNi high-entropy alloy has a delayed diffusion effect, and in the diffusion welding process, the diffusion speed of metal elements in the nickel-based high-temperature alloy to the high-entropy alloy is low, so that the violent mutual diffusion of the elements at the interface between the base metal and the intermediate layer can be controlled, the recrystallization of a near seam region of the single-crystal high-temperature alloy base metal caused by excessive diffusion of the interface elements is avoided, and the performance of the base metal is ensured;
(4) the high entropy effect of the intermediate layer enables the welding line to be in a solid solution structure, and ensures that the joint keeps higher plasticity of the solid solution.
Drawings
In order to more clearly illustrate the technical solutions of the embodiments of the present invention, the drawings needed to be used in the embodiments will be briefly described below, it should be understood that the following drawings only illustrate some embodiments of the present invention and therefore should not be considered as limiting the scope, and for those skilled in the art, other related drawings can be obtained according to the drawings without inventive efforts.
FIG. 1 is a side-enlarged view of FGH98 powder superalloy of the material obtained by diffusion welding in example 1 of the present invention;
FIG. 2 is a diagram showing the enlarged observation result of the single crystal side of DD5 of the material obtained by diffusion welding in example 1 of the present invention;
FIG. 3 is a side-enlarged view of FGH98 powder superalloy of the material obtained by diffusion welding comparative example 1 of the present invention;
FIG. 4 is a graph showing the enlarged observation result of the single crystal side of DD5 of the material obtained by diffusion welding comparative example 1 of the present invention;
fig. 5 is a schematic position diagram of FGH98, DD5, high entropy alloy mass in diffusion welding provided by the embodiment of the invention.
Detailed Description
In order to make the objects, technical solutions and advantages of the embodiments of the present invention clearer, the technical solutions in the embodiments of the present invention will be clearly and completely described below. The examples, in which specific conditions are not specified, were conducted under conventional conditions or conditions recommended by the manufacturer. The reagents or instruments used are not indicated by the manufacturer, and are all conventional products available commercially.
The present embodiment provides a method of diffusion bonding, comprising the steps of:
and performing diffusion welding on the IC10 single crystal and the nickel-based high-temperature alloy by using AlCoCrFeNi series high-entropy alloy as an intermediate layer. The inventor finds that the AlCoCrFeNi series high-entropy alloy is used as the intermediate layer of diffusion welding to inhibit the precipitation of interface carbide, and then the bonding strength of the welding position is improved. Meanwhile, the metal of the base metal can be reduced from being diluted in the welding seam area, the recrystallization of the base metal is reduced, and the performance of the near seam area is improved. And the bonding strength of the high-entropy alloy and the gamma' phase in the CI10 single crystal and the nickel-based superalloy can be ensured.
Wherein the welding process may be diffusion welding, in particular:
firstly, FGH98, DD5 and high entropy alloy are respectively processed into 10 multiplied by 15 multiplied by 3mm by a wire cut electrical discharge machine3、5×5×5mm3、10×10×1mm3A rectangular parallelepiped;
secondly, before the experiment, the surfaces to be welded are gradually polished by sand paper according to 240#, 400#, 600#, 1000#, and 1500#, then the surfaces are immersed in alcohol for ultrasonic cleaning for three minutes, and then the surfaces are dried by cold air;
thirdly, assembling the sample according to the mode of figure 5, rapidly putting the sample into a furnace, applying initial pressure to enable the surfaces to be tightly contacted, closing a furnace door and an exhaust valve, vacuumizing, designing a heating program according to set process parameters, and starting cooling circulating water. When the vacuum degree in the furnace reaches 3.5 multiplied by 10-2And when Pa, operating a heating program to weld. And after welding, cooling the welding material to room temperature along with the furnace, and then sampling.
Alternatively, other diffusion welding methods may be used.
Further, the conditions of diffusion welding are: the welding temperature is 900-. The temperature, pressure, holding time and the like of diffusion welding have great influence on the welding quality.
Specifically, in the embodiment of the invention, if the welding temperature is higher than 900 ℃, the yield strength of the AlCoCrFeNi series high-entropy alloy in the middle layer can be obviously reduced, and the full bonding of the interface between the middle layer and the base material can be ensured by performing diffusion welding at the temperature; for the FGH98 powder superalloy, the temperature higher than 1138 ℃ causes a great deal of dissolution of precipitated phase, so the diffusion welding temperature is 900-1130 ℃.
In diffusion welding, pressure can promote the original surface to be welded to be tightly attached, so that the local part of the sample generates plastic deformation, mutual diffusion of atoms on two sides of an interface is facilitated, and the welding quality of the joint is improved. However, excessive pressure can cause severe plastic deformation of the joint, which affects the welding precision of workpieces. Therefore, the diffusion connection with the intermediate layer made of the high-temperature alloy and the high-entropy alloy is performed under the conditions of 5-15MPa and the heat preservation time of 1-2 h.
Specifically, the IC10 single crystal includes DD5 single crystal. The nickel-based superalloy is an FGH98 powder alloy. The main constituent elements of the DD5 single crystal and FGH98 powder alloy are Ni, Co and Al, so that the AlCoCrFeNi high-entropy alloy can exert the effect thereof, and the performance of a welded finished product is improved.
It should be noted that the DD5 single crystal and FGH98 powder alloy used in the embodiment of the present invention may be DD5 single crystal and FGH98 powder alloy that are directly purchased from the market.
Further, the AlCoCrFeNi high-entropy alloy adopted by the embodiment of the invention comprises the following components in atomic percent: 0.3 at% of Al, and the balance of Co, Cr, Fe and Ni, wherein the atomic ratio of Co, Cr, Fe and Ni is 1:1: 1. That is, the AlCoCrFeNi-based high entropy alloy contains Al, Co, Cr, Fe, and Ni, except inevitable impurity elements.
The composition and content of metal elements in the AlCoCrFeNi high-entropy alloy are controlled to influence the performance of the alloy as the intermediate layer, namely the AlCoCrFeNi high-entropy alloy with the components and the proportion limited in the embodiment of the invention can further inhibit the precipitation of carbide, reduce the diffusion speed of base metal elements such as Fe, Al, Cr, Ta and Mo to the high-entropy alloy, avoid recrystallization of a near seam region of a monocrystalline high-temperature alloy base metal caused by excessive diffusion of interface elements and ensure the performance of the base metal.
Further, since the AlCoCrFeNi-based high-entropy alloy is used as an intermediate layer in diffusion welding, and the grain size of the material of the intermediate layer also has an influence on the diffusion welding, the grain diameter of the AlCoCrFeNi-based high-entropy alloy is limited to 1 to 10 micrometers in the embodiment of the present invention. The AlCoCrFeNi series high-entropy alloy with the grain size is beneficial to improving the performance of the alloy, and then the performance of the material obtained after diffusion welding is improved.
Further, the AlCoCrFeNi high-entropy alloy is prepared by mixing an aluminum source, a cobalt source, a chromium source, an iron source and a nickel source, smelting, and then performing heat treatment to form the AlCoCrFeNi high-entropy alloy. The method comprises the following specific steps:
the non-consumable vacuum arc melting method is selected for melting and preparing the high-entropy alloy: taking 70g of prepared alloy as an example, weighed metal particles are placed in a crucible of a smelting furnace according to the melting point, wherein Al (0.101g), Co (18.355g), Cr (15.867g), Fe (17.396g) and Ni (18.281g) are placed in sequence from top to bottom (the metal particles are placed at the end with high melting point and on the surface and are easy to be in arc contact).
Firstly, equipment is vacuumized;
before smelting, whether all gas valves are closed, whether water circulation is started, whether a main power switch is started and whether argon in a smelting furnace reaches-0.05 Pa are checked;
moving the electrode to a position 2mm above the sponge titanium in the smelting chamber for arc striking, lifting the electrode tip to a position 1cm away from the surface of the sponge titanium after the arc striking is successful, and smelting the sponge titanium for 3min for adsorbing oxygen in the furnace;
and fourthly, rapidly moving the electrode successfully ignited to a position 1cm above the crucible where the sample to be smelted is located, and smelting the sample. And in the smelting process, the electrode tip is required to slowly move back and forth on the surface of the sample, so that the surface of the sample is uniformly heated until the sample is completely melted to the bottom surface of the crucible, an even disc shape is formed, then the current is closed, the sample is cooled down from red to red, the sample is turned over, the electrode is moved to the upper part of the titanium sponge for arc striking again, the sample is smelted again, each sample is smelted at least four times, and finally the high-entropy alloy button ingot is obtained.
And then heat treatment is carried out, the heat treatment adopted here being the conventional annealing operation such as homogenization and rolling.
Preferably, the conditions for forming the AlCoCrFeNi series high-entropy alloy by heat treatment comprise the following steps: the homogenization temperature is 1200 ℃, the homogenization time is 4 hours, the rolling reduction is 60 percent, and the temperature for heat preservation after rolling is 850 ℃. The AlCoCrFeNi series high-entropy alloy prepared by adopting the heat treatment conditions has uniform components, the obtained high-entropy alloy has proper grain size, and the performance of the AlCoCrFeNi series high-entropy alloy as an intermediate layer is improved.
The AlCoCrFeNi-based high-entropy alloy provided by the embodiment of the invention can be prepared according to the method or can be directly purchased.
The embodiment of the invention also provides a welding finished product which is prepared by the diffusion welding method in any one of the previous embodiments.
The features and properties of the present invention are described in further detail below with reference to examples.
Example 1
The present embodiments provide a method of diffusion welding, comprising: and performing diffusion welding on the DD5 single crystal and the FGH98 powder alloy by using AlCoCrFeNi series high-entropy alloy as an intermediate layer.
The AlCoCrFeNi high-entropy alloy comprises the following components in atomic percent: 0.3 at% of Al0, and the balance of Co, Cr, Fe and Ni, wherein the atomic ratio of Co, Cr, Fe and Ni is 1:1: 1. The grain diameter of the AlCoCrFeNi series high-entropy alloy is 5-10 microns.
The preparation method of the AlCoCrFeNi high-entropy alloy in the embodiment comprises the following steps: as described above, the conditions of the heat treatment system were: the homogenization temperature is 1200 ℃, the homogenization time is 4 hours, the rolling is reduced by 60 percent, the annealing system after rolling is that the temperature for heat preservation is 850 ℃, 1 hour, and then water quenching is carried out.
The conditions for diffusion welding were: the welding temperature is 1050 ℃, the welding pressure is 5Mpa, and the heat preservation time is 1 hour.
The embodiment also provides a welding finished product, which is obtained by the method.
Example 2 to example 3
Examples 2 and 3 each provide a method of diffusion bonding that is substantially identical to the method of diffusion bonding provided in example 1 except that the specific operating conditions are different as follows:
example 2: the grain diameter of the AlCoCrFeNi series high-entropy alloy is 1-7 microns. The conditions for diffusion welding were: the welding temperature is 900 ℃, the welding pressure is 15MPa, and the heat preservation time is 2 hours.
Example 3: the grain diameter of the AlCoCrFeNi series high-entropy alloy is 1-7 microns. The conditions for diffusion welding were: the welding temperature is 1130 ℃, the welding pressure is 10MPa, and the heat preservation time is 1.5 hours.
Comparative example 1: diffusion welding was performed according to the diffusion welding method provided in example 1, except that the high-entropy alloy used was Fe39Mn20Co20Cr15Si5Al1。
The materials obtained after diffusion welding of example 1 were characterized, and the results of the measurements are shown in fig. 1 and 2. FIG. 1 is a side view of the FGH98 powder superalloy, and FIG. 2 is a side view of DD5 single crystal.
According to the fig. 1 and fig. 2, the existence of the intermediate layer AlCoCrFeNi high-entropy alloy realizes the connection of the DD5 single crystal and the FGH98 powder high-temperature alloy under the condition that no carbide appears at the interface, that is, the high-entropy alloy is adopted as the intermediate layer, so that the carbide precipitation at the diffusion interface can be effectively inhibited. Meanwhile, the DD5 single crystal and the single crystal at the high-entropy alloy interface are basically kept unchanged, and recrystallization is not obvious. In addition, a small amount of compound phase is formed in the near-interface region.
The material obtained after diffusion welding of comparative example 1 was characterized, and the test results are shown in fig. 3 and 4. FIG. 1 is a side view of the FGH98 powder superalloy, and FIG. 2 is a side view of DD5 single crystal.
As can be seen from FIG. 3, Fe39Mn20Co20Cr15Si5Al1The addition of the intermediate layer realizes the connection of DD5 single crystal and FGH98 powder superalloy, but unwelded holes appear on an FGH98 and high-entropy connection interface, and more compounds are generated in a near interface region; carbide is generated at the interface of the DD5 single crystal and the high-entropy alloy, and the interface of a diffusion layer and the DD5 parent material structure is quite obvious. The AlCoCrFeNi series high-entropy alloy is beneficial to reducing the formation of carbides, improving the strength of the welded material, reducing the dilution of alloy solute in a near seam region of a base material and improving the performance of the near seam region.
Shear tests were performed on example 1 and comparative example 1. The results of the tests are shown in the following table:
according to the table, the fracture is located in the high-entropy alloy middle layer, namely the high-entropy alloy and the parent metals on the two sides are reliably connected. Meanwhile, as is clear from the data of comparative example 1 and comparative example 1, a welded joint having more excellent performance can be obtained by using the AlCoCrFeNi-based high-entropy intermediate layer.
The above description is only a preferred embodiment of the present invention and is not intended to limit the present invention, and various modifications and changes may be made by those skilled in the art. Any modification, equivalent replacement, or improvement made within the spirit and principle of the present invention should be included in the protection scope of the present invention.
Claims (9)
1. A method of diffusion welding, comprising: and performing diffusion welding on the IC10 single crystal and the nickel-based high-temperature alloy by using AlCoCrFeNi series high-entropy alloy as an intermediate layer.
2. The method of diffusion welding of claim 1, wherein the composition of said AlCoCrFeNi series high entropy alloy comprises, in atomic percent: 0.3 at% of Al, and the balance of Co, Cr, Fe and Ni, wherein the atomic ratio of Co, Cr, Fe and Ni is 1:1: 1.
3. The method of diffusion welding of claim 1, wherein said AlCoCrFeNi-based high entropy alloy has a grain diameter of 1-10 microns.
4. The diffusion welding method of any one of claims 1 to 3, wherein the AlCoCrFeNi-based high entropy alloy is prepared by a process comprising: mixing an aluminum source, a cobalt source, a chromium source, an iron source and a nickel source, smelting, and then carrying out heat treatment to form the AlCoCrFeNi high-entropy alloy.
5. The method of diffusion welding of claim 4, wherein the conditions for heat treating to form the AlCoCrFeNi-based high entropy alloy comprise: the homogenization temperature is 1200 ℃, the homogenization time is 4 hours, the rolling is reduced by 60 percent, the temperature for heat preservation after rolling is 850 ℃, and the heat preservation time is 1 hour.
6. The method of diffusion bonding of claim 1 wherein said IC10 single crystal comprises DD5 single crystal.
7. The method of diffusion welding of claim 1, wherein said nickel-base superalloy is a FGH98 powder alloy.
8. The method of diffusion welding of claim 1, wherein the conditions of diffusion welding are: the welding temperature is 900-.
9. A welded product, characterized in that it is produced by a method of diffusion welding according to any one of claims 1-8.
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Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113182632A (en) * | 2021-05-07 | 2021-07-30 | 浙江工业大学 | Method for connecting C/C composite material by adopting high-entropy alloy brazing |
| CN115178914A (en) * | 2022-06-22 | 2022-10-14 | 西北工业大学 | For Ti 2 AlNb intermetallic compound diffusion welding high-entropy interlayer and preparation method |
| CN116984725A (en) * | 2023-09-27 | 2023-11-03 | 中国航发沈阳黎明航空发动机有限责任公司 | FGH98 alloy diffusion welding method added with pure nickel foil interlayer |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20170314097A1 (en) * | 2016-05-02 | 2017-11-02 | Korea Advanced Institute Of Science And Technology | High-strength and ultra heat-resistant high entropy alloy (hea) matrix composites and method of preparing the same |
| CN108299006A (en) * | 2018-01-24 | 2018-07-20 | 北京工业大学 | A kind of method of compound high entropy solder coated laser ceramic soldering and metal |
| CN108754463A (en) * | 2018-06-13 | 2018-11-06 | 太原理工大学 | A method of improving face-centred cubic structure high-entropy alloy tensile strength |
| CN109955004A (en) * | 2019-04-30 | 2019-07-02 | 上海交通大学 | A kind of high entropy alloy material and application for welding |
| CN110125573A (en) * | 2019-06-18 | 2019-08-16 | 东莞理工学院 | A kind of ferro-cobalt Ni-Cr-Mn high-entropy alloy solder and preparation method thereof |
-
2020
- 2020-09-17 CN CN202010978544.0A patent/CN112077430B/en active Active
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20170314097A1 (en) * | 2016-05-02 | 2017-11-02 | Korea Advanced Institute Of Science And Technology | High-strength and ultra heat-resistant high entropy alloy (hea) matrix composites and method of preparing the same |
| CN108299006A (en) * | 2018-01-24 | 2018-07-20 | 北京工业大学 | A kind of method of compound high entropy solder coated laser ceramic soldering and metal |
| CN108754463A (en) * | 2018-06-13 | 2018-11-06 | 太原理工大学 | A method of improving face-centred cubic structure high-entropy alloy tensile strength |
| CN109955004A (en) * | 2019-04-30 | 2019-07-02 | 上海交通大学 | A kind of high entropy alloy material and application for welding |
| CN110125573A (en) * | 2019-06-18 | 2019-08-16 | 东莞理工学院 | A kind of ferro-cobalt Ni-Cr-Mn high-entropy alloy solder and preparation method thereof |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113182632A (en) * | 2021-05-07 | 2021-07-30 | 浙江工业大学 | Method for connecting C/C composite material by adopting high-entropy alloy brazing |
| CN115178914A (en) * | 2022-06-22 | 2022-10-14 | 西北工业大学 | For Ti 2 AlNb intermetallic compound diffusion welding high-entropy interlayer and preparation method |
| CN115178914B (en) * | 2022-06-22 | 2024-01-16 | 西北工业大学 | For Ti 2 AlNb intermetallic compound diffusion welding high-entropy middle layer and preparation method thereof |
| CN116984725A (en) * | 2023-09-27 | 2023-11-03 | 中国航发沈阳黎明航空发动机有限责任公司 | FGH98 alloy diffusion welding method added with pure nickel foil interlayer |
| CN116984725B (en) * | 2023-09-27 | 2023-12-01 | 中国航发沈阳黎明航空发动机有限责任公司 | FGH98 alloy diffusion welding method added with pure nickel foil interlayer |
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